CN105272248A - Preparation method of crack self-healing ceramic material - Google Patents
Preparation method of crack self-healing ceramic material Download PDFInfo
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- CN105272248A CN105272248A CN201510771262.2A CN201510771262A CN105272248A CN 105272248 A CN105272248 A CN 105272248A CN 201510771262 A CN201510771262 A CN 201510771262A CN 105272248 A CN105272248 A CN 105272248A
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- healing
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- crackle
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Abstract
The invention relates to a preparation method of a crack self-healing ceramic material. The problem that an existing TZP material is lowered in strength and toughness at a high temperature is solved. The method includes the steps of adding second-phase self-healing particles to base body powder, adding absolute ethyl alcohol, conducting ball milling for 24 h through a blender mixer, conducting drying and screening to obtain mixed powder, sintering the mixed powder through a vacuum hot-press method, and obtaining the crack self-healing ceramic material. The method is low in raw material cost, simple in preparation process and short in cycle; by means of the added SiC and MoSi2 particles, the mechanical properties of the composite material can be improved, and cracks can be healed, and cracks can be healed through the non-crystalline Si-O(SiO) phase generated through oxidation; the heat treatment process adopted for crack healing is easy and convenient to operate, low in cost and wide in application range; after the cracks are healed, the material strength reaches the strength of a sintering sample. The method is applied to the field of ceramic materials.
Description
Technical field
The present invention relates to a kind of preparation method of crackle self-healing stupalith.
Background technology
Since Gupta reported first since tetragonal zircite ceramic (TZP), the research of TZP material is the problem of awfully hot door always.TZP pottery is tetragonal zirconia polycrystal material, there is higher room temperature strength and fracture toughness property, there is higher hardness in addition, good wear resistance, chemical resistance, often be applied to harsh and unforgiving environments and harsh loading condition, as being used as the cutting knife etc. of cam, glass fibre and tape in wortle, bearing, sealing member, engine piston top, valve mechanism.But regrettably, TZP still belongs to hard brittle material; Simultaneously because stress-induced phase transformation is to the susceptibility of temperature, make t-ZrO under high temperature
2stability increase, cause transformation toughening to lose efficacy and cause the intensity of material and toughness rise with temperature and sharply decline, largely reducing the competitive edge of itself and metallic substance, limit scale development and the application of this material.
Summary of the invention
The present invention is the problem that will solve at high temperature intensity and the toughness decline of existing TZP material, provides a kind of preparation method of crackle self-healing stupalith.
The preparation method of a kind of crackle self-healing of the present invention stupalith, carries out according to the following steps:
One, added in matrix powder by second-phase self-healing particle, add dehydrated alcohol mixer ball milling 24h post-drying and sieve, obtain mixed powder, wherein in mixed powder, the ratio of second-phase self-healing particle is 10 ~ 20vol%; Two, mixed powder adopts vacuum hot-pressing sintering, and sintering temperature 1500 ~ 1600 DEG C, pressure 30MPa, pressurize 0.5 ~ 1.5h, obtain crackle self-healing stupalith.
The present invention has the Second Phase Particle of crackle self-healing capability by adding in body material, under certain condition can healed cracks, restorer intensity.Matrix material is in preparation and applied at elevated temperature process, and the second-phase self-healing particle added in material is subject to the protection of matrix oxide ceramics, does not reach oxidizing atmosphere can completely and is present in material internal.Once there be crackle to produce, just provide a passage oxygen and enter into material internal, with the self-healing particle generation oxidizing reaction being present in fracture edges, the oxidation products of generation fills up crackle, improves the strength of materials.MoSi
2have that hot strength is high, hardness is high, wear-resistant, corrosion-resistant, antioxidant property is good, thermal conductivity is high with SiC material and over-all properties that Heat stability is good etc. is excellent, joined in TZ3Y20A body material, refinement matrix grain, strengthening crystal boundary can be played, strengthen t-ZrO
2stablize mutually, and the deflection to crackle, the effect of overseas Chinese federation, improves the strength of materials.
SiC, MoSi
2particle not only can improve the mechanical property of matrix material in theory, is also important crackle self-healing particle.SiC belongs to middle temperature self-healing material, and at high temperature oxidation generates SiO
2, one deck glassiness protective membrane can be formed, effectively stop the scattering and permeating of oxygen, therefore there is certain self-healing character.MoSi
2be a kind of material at high temperature self-healing material of most study, its mode of oxidizing and product are subject to the impact of oxygen partial pressure and temperature.Can be there is significant reduction in the crackle of the composite inner after pyroprocessing and hole, its cardinal principle make use of SiC, MoSi
2at high temperature occur to be oxidized and fill internal void thus reach the effect of self-healing.SiC, MoSi
2all can there is oxidizing reaction under certain condition, generate oxidation products SiO
2, this oxide compound can be filled up in crackle, healed cracks.Chemical reaction occurs and can not introduce other element pollution material systems, in addition, oxidizing reaction is thermopositive reaction, and the heat of release can make oxidation products be combined closely with crackle wall, makes up fault in material and improves intensity.
The invention has the beneficial effects as follows:
1, raw materials cost is low, and preparation technology is simple, and the cycle is short;
2, SiC, MoSi of adding
2particle can not only improve the mechanical property of matrix material, also can healed cracks, amorphous Si – O (SiO) the phase healed cracks that oxidation generates;
3, the thermal treatment process of healed cracks employing is simple to operate, and convenient, cost is low, applied range.
4, after crack healing, the strength of materials reaches sintered specimen intensity, and crackle self-healing solves stupalith affects reliability most effective means owing to cracking in use procedure.
Accompanying drawing explanation
Fig. 1 is crackle self-healing stupalith and the XRD figure of pure body material of the preparation of embodiment 2, embodiment 3 and embodiment 4, and wherein ■ is α – Al
2o
3, ◆ be t – ZrO
2, ▲ for β-SiC, ★ be c – ZrO
2;
Fig. 2 is that the crackle self-healing stupalith of pure body material TZ3Y20A and embodiment 3 preparation is with heat treatment time variation relation figure, wherein ■ is the Specimens of crackle self-healing stupalith, ● be the Specimens of pure body material TZ3Y20A, a is the precracked specimen of crackle self-healing stupalith, b is the precracked specimen of pure body material TZ3Y20A, is the crack healing sample of crackle self-healing stupalith, and zero is the crack healing sample of pure body material TZ3Y20A.
Embodiment
Embodiment one: the preparation method of a kind of crackle self-healing of present embodiment stupalith, carry out according to the following steps:
One, added in matrix powder by second-phase self-healing particle, add dehydrated alcohol mixer ball milling 24h post-drying and sieve, obtain mixed powder, wherein in mixed powder, the ratio of second-phase self-healing particle is 10 ~ 20vol%; Two, mixed powder adopts vacuum hot-pressing sintering, and sintering temperature 1500 ~ 1600 DEG C, pressure 30MPa, pressurize 0.5 ~ 1.5h, obtain crackle self-healing stupalith.
Present embodiment has the Second Phase Particle of crackle self-healing capability by adding in body material, under certain condition can healed cracks, restorer intensity.Matrix material is in preparation and applied at elevated temperature process, and the second-phase self-healing particle added in material is subject to the protection of matrix oxide ceramics, does not reach oxidizing atmosphere can completely and is present in material internal.Once there be crackle to produce, just provide a passage oxygen and enter into material internal, with the self-healing particle generation oxidizing reaction being present in fracture edges, the oxidation products of generation fills up crackle, improves the strength of materials.MoSi
2have that hot strength is high, hardness is high, wear-resistant, corrosion-resistant, antioxidant property is good, thermal conductivity is high with SiC material and over-all properties that Heat stability is good etc. is excellent, joined in TZ3Y20A body material, refinement matrix grain, strengthening crystal boundary can be played, strengthen t-ZrO
2stablize mutually, and the deflection to crackle, the effect of overseas Chinese federation, improves the strength of materials.
SiC, MoSi
2particle not only can improve the mechanical property of matrix material in theory, is also important crackle self-healing particle.SiC belongs to middle temperature self-healing material, and at high temperature oxidation generates SiO
2, one deck glassiness protective membrane can be formed, effectively stop the scattering and permeating of oxygen, therefore there is certain self-healing character.MoSi
2be a kind of material at high temperature self-healing material of most study, its mode of oxidizing and product are subject to the impact of oxygen partial pressure and temperature.Can be there is significant reduction in the crackle of the composite inner after pyroprocessing and hole, its cardinal principle make use of SiC, MoSi
2at high temperature occur to be oxidized and fill internal void thus reach the effect of self-healing.SiC, MoSi
2all can there is oxidizing reaction under certain condition, generate oxidation products SiO
2, this oxide compound can be filled up in crackle, healed cracks.Chemical reaction occurs and can not introduce other element pollution material systems, in addition, oxidizing reaction is thermopositive reaction, and the heat of release can make oxidation products be combined closely with crackle wall, makes up fault in material and improves intensity.
The beneficial effect of present embodiment is:
1, raw materials cost is low, and preparation technology is simple, and the cycle is short;
2, SiC, MoSi of adding
2particle can not only improve the mechanical property of matrix material, also can healed cracks, amorphous Si – O (SiO) the phase healed cracks that oxidation generates;
3, the thermal treatment process of healed cracks employing is simple to operate, and convenient, cost is low, applied range.
4, after crack healing, the strength of materials reaches sintered specimen intensity, and crackle self-healing solves stupalith affects reliability most effective means owing to cracking in use procedure.
Embodiment two: present embodiment and embodiment one unlike: in step one, second-phase self-healing particle is MoSi
2or SiC.Other is identical with embodiment one.
Embodiment three: present embodiment and embodiment one or two unlike: the matrix powder described in step one is TZ3Y20A.Other is identical with embodiment one or two.
Embodiment four: one of present embodiment and embodiment one to three unlike: sieving described in step one referred to 150 mesh sieves.Other is identical with one of embodiment one to three.
Embodiment five: one of present embodiment and embodiment one to four unlike: in step 2, sintering temperature is 1550 DEG C.In step 2, the dwell time is 1h.Other is identical with one of embodiment one to four.
Embodiment six: one of present embodiment and embodiment one to five unlike: in step 2, the dwell time is 1h.Other is identical with one of embodiment one to five.
The following examples will be further described the present invention, but not thereby limiting the invention.
Embodiment 1: the preparation method of a kind of crackle self-healing of the present embodiment stupalith, carry out according to the following steps:
One, add in TZ3Y20A by SiC, add dehydrated alcohol mixer ball milling 24h post-drying and cross 150 mesh sieves, obtain mixed powder, wherein in mixed powder, the ratio of second-phase self-healing particle is 10vol%; Two, mixed powder adopts vacuum hot-pressing sintering, and sintering temperature 1550 DEG C, pressure 30MPa, pressurize 1h, obtain crackle self-healing stupalith.
It is rectangular that the crackle self-healing stupalith inner diamond slicing machine prepared by the present embodiment is cut into 3 × 4 × 20mm, and surface is through grinding and polishing process, and in bending resistance experiment, tension face center utilizes Vickers hardness tester precast length about 120 μm of crackles; (4) sample thermal treatment in High Temperature Furnaces Heating Apparatus of crackle, thermal treatment temp 800 DEG C, time 30h will be prefixed; (5) sample after thermal treatment is carried out room temperature bending strength test, intensity reaches sintered specimen intensity, illustrates that crackle heals completely.
Embodiment 2: the preparation method of a kind of crackle self-healing of the present embodiment stupalith, carry out according to the following steps:
One, add in TZ3Y20A by SiC, add dehydrated alcohol mixer ball milling 24h post-drying and cross 150 mesh sieves, obtain mixed powder, wherein in mixed powder, the ratio of second-phase self-healing particle is 15vol%; Two, mixed powder adopts vacuum hot-pressing sintering, and sintering temperature 1550 DEG C, pressure 30MPa, pressurize 1h, obtain crackle self-healing stupalith.
It is rectangular that the crackle self-healing stupalith inner diamond slicing machine prepared by the present embodiment is cut into 3 × 4 × 20mm, and surface is through grinding and polishing process, and in bending resistance experiment, tension face center utilizes Vickers hardness tester precast length about 120 μm of crackles; (4) sample thermal treatment in High Temperature Furnaces Heating Apparatus of crackle, thermal treatment temp 1000 DEG C, time 5h will be prefixed; (5) sample after thermal treatment is carried out room temperature bending strength test, intensity reaches sintered specimen intensity, illustrates that crackle heals completely.
Embodiment 3: the preparation method of a kind of crackle self-healing of the present embodiment stupalith, carry out according to the following steps:
One, add in TZ3Y20A by SiC, add dehydrated alcohol mixer ball milling 24h post-drying and cross 150 mesh sieves, obtain mixed powder, wherein in mixed powder, the ratio of second-phase self-healing particle is 20vol%; Two, mixed powder adopts vacuum hot-pressing sintering, and sintering temperature 1550 DEG C, pressure 30MPa, pressurize 1h, obtain crackle self-healing stupalith.
Embodiment 4: the preparation method of a kind of crackle self-healing of the present embodiment stupalith, carry out according to the following steps:
One, add in TZ3Y20A by SiC, add dehydrated alcohol mixer ball milling 24h post-drying and cross 150 mesh sieves, obtain mixed powder, wherein in mixed powder, the ratio of second-phase self-healing particle is 10vol%; Two, mixed powder adopts vacuum hot-pressing sintering, and sintering temperature 1550 DEG C, pressure 30MPa, pressurize 1h, obtain crackle self-healing stupalith.
It is rectangular that the crackle self-healing stupalith inner diamond slicing machine prepared by the present embodiment is cut into 3 × 4 × 20mm, and surface is through grinding and polishing process, and in bending resistance experiment, tension face center utilizes Vickers hardness tester precast length about 120 μm of crackles; (4) sample thermal treatment in High Temperature Furnaces Heating Apparatus of crackle, thermal treatment temp 1000 DEG C, time 10h will be prefixed; (5) sample after thermal treatment is carried out room temperature bending strength test, intensity reaches sintered specimen intensity, illustrates that crackle heals completely.
Crackle self-healing stupalith and the pure body material of the preparation of embodiment 2, embodiment 3 and embodiment 4 carry out XRD analysis, result as shown in Figure 1, in figure, 0Vol.% representative is the pure body material not adding second-phase self-healing particle, as shown in Figure 1, adopt vacuum heating-press sintering method, image does not change, and the complete preservation of the second-phase of interpolation in the base.
With heat treatment time variation relation as shown in Figure 2, TZ3Y20A stupalith does not all reach Specimens intensity to crackle self-healing stupalith prepared by pure body material TZ3Y20A and the present embodiment under any heat treatment time, illustrates that crackle does not heal completely.TZ3Y20A stupalith is without intensity during precrack higher (average 1120MPa), after precrack, strength degradation is a lot, only have 31% of original intensity, after different time thermal treatment, although intensity increases than pre-flawed specimen, but still well below Specimens intensity, more changqiang degree is higher for heat treatment time, and during 20h, intensity is the highest returns to 592MPa.Observe fracture surface of sample position, find that fracture all occurs in precrack place.Carry out XRD detection to sample after thermal treatment in addition, thing does not change mutually, does not have cenotype to produce and also ZrO does not occur
2phase transformation.Increase through heat treatment material intensity, illustrate and at high temperature rely on molecular diffusion to contribute to healed cracks, heat treatment time is longer, spreads more abundant, but diffusive healing limited efficiency, the t – ZrO in body material
2he α – Al
2o
3there is no the ability of complete healed cracks mutually.
Under identical heat-treat condition, TZ3Y20A – 10vol%SiC composite ceramic material extends to 10h from 5h along with heat treatment time, bending strength also increases, and exceed Specimens intensity as thermal treatment 10h, under this heat-treat condition is described, crackle heals completely.Contrast this two kinds of stupaliths, under identical heat-treat condition, composite material strength, all higher than pure body material, illustrates that the second-phase SiC added has the ability of healed cracks, can complete healed cracks under suitable heat-treat condition.The second-phase self-healing particulate oxidation added generates amorphous Si – O (SiO) phase, and healed cracks makes intensity recover; In addition SiC/MoSi
2oxidizing reaction is thermopositive reaction, and the heat of release can accelerate oxidation and the diffusion of neighboring atom; ZrO in material under high temperature
2and Al
2o
3the diffusion of atom also plays a role to crack healing, and wherein oxidizing reaction healing is main healing mechanism.
Embodiment 5: the preparation method of a kind of crackle self-healing of the present embodiment stupalith, carry out according to the following steps:
One, add in TZ3Y20A by SiC, add dehydrated alcohol mixer ball milling 24h post-drying and cross 150 mesh sieves, obtain mixed powder, wherein in mixed powder, the ratio of second-phase self-healing particle is 10vol%; Two, mixed powder adopts vacuum hot-pressing sintering, and sintering temperature 1550 DEG C, pressure 30MPa, pressurize 1h, obtain crackle self-healing stupalith.
It is rectangular that the crackle self-healing stupalith inner diamond slicing machine prepared by the present embodiment is cut into 3 × 4 × 20mm, and surface is through grinding and polishing process, and in bending resistance experiment, tension face center utilizes Vickers hardness tester precast length about 120 μm of crackles; (4) sample thermal treatment in High Temperature Furnaces Heating Apparatus of crackle, thermal treatment temp 1100 DEG C, time 5h will be prefixed; (5) sample after thermal treatment is carried out room temperature bending strength test, intensity reaches sintered specimen intensity, illustrates that crackle heals completely.
From above the present embodiment, raw materials cost of the present invention is low, and preparation technology is simple, and the cycle is short; SiC, MoSi of adding
2particle can not only improve the mechanical property of matrix material, also can healed cracks, amorphous Si – O (SiO) the phase healed cracks that oxidation generates; The thermal treatment process that healed cracks adopts is simple to operate, and convenient, cost is low, applied range.After crack healing, the strength of materials reaches sintered specimen intensity, and crackle self-healing solves stupalith affects reliability most effective means owing to cracking in use procedure.
Claims (6)
1. a preparation method for crackle self-healing stupalith, is characterized in that the method is carried out according to the following steps:
One, added in matrix powder by second-phase self-healing particle, add dehydrated alcohol mixer ball milling 24h post-drying and sieve, obtain mixed powder, wherein in mixed powder, the ratio of second-phase self-healing particle is 10 ~ 20vol%; Two, mixed powder adopts vacuum hot-pressing sintering, and sintering temperature 1500 ~ 1600 DEG C, pressure 30MPa, pressurize 0.5 ~ 1.5h, obtain crackle self-healing stupalith.
2. the preparation method of a kind of crackle self-healing stupalith according to claim 1, is characterized in that in step one, second-phase self-healing particle is MoSi
2or SiC.
3. the preparation method of a kind of crackle self-healing stupalith according to claim 1, is characterized in that the matrix powder described in step one is TZ3Y20A.
4. the preparation method of a kind of crackle self-healing stupalith according to claim 1, is characterized in that sieving described in step one referred to 150 mesh sieves.
5. the preparation method of a kind of crackle self-healing stupalith according to claim 1, is characterized in that in step 2, sintering temperature is 1550 DEG C.
6. the preparation method of a kind of crackle self-healing stupalith according to claim 1, is characterized in that in step 2, the dwell time is 1h.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108165929A (en) * | 2017-12-28 | 2018-06-15 | 中国科学院宁波材料技术与工程研究所 | A kind of self-healing coating and preparation method and application |
| CN108395223A (en) * | 2018-03-22 | 2018-08-14 | 中铭瓷(苏州)纳米粉体技术有限公司 | A kind of MAX phases crackle self-healing ceramic material and preparation method thereof |
| CN109608218A (en) * | 2019-01-28 | 2019-04-12 | 中国人民解放军国防科技大学 | Self-healing ceramic matrix composite and low-temperature rapid preparation method thereof |
| CN109987947A (en) * | 2019-04-19 | 2019-07-09 | 中国科学院上海硅酸盐研究所 | Utilize the thermally conductive method with mechanical property of in-situ stress induced transformation Synchronous fluorimetry aluminum oxide coating layer |
| CN111548164A (en) * | 2020-05-19 | 2020-08-18 | 中钢集团洛阳耐火材料研究院有限公司 | Continuous self-toughening nitride-bonded silicon carbide refractory material |
| CN113402263A (en) * | 2021-07-02 | 2021-09-17 | 海南大学 | Alumina-based composite ceramic and preparation method thereof |
| EP3885089A4 (en) * | 2018-12-21 | 2022-08-17 | Canon Kabushiki Kaisha | Powdered inorganic material and method for producing structure |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101265119A (en) * | 2008-04-29 | 2008-09-17 | 天津大学 | Method for bonding zirconium oxide sintered body |
| CN101565306A (en) * | 2009-05-21 | 2009-10-28 | 济南大学 | Zirconia ceramic matrix composite and preparation method thereof |
| CN101857455A (en) * | 2010-06-25 | 2010-10-13 | 中南大学 | High strength and toughness 3Y-TZP composite ceramic and preparation method thereof |
-
2015
- 2015-11-12 CN CN201510771262.2A patent/CN105272248A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101265119A (en) * | 2008-04-29 | 2008-09-17 | 天津大学 | Method for bonding zirconium oxide sintered body |
| CN101565306A (en) * | 2009-05-21 | 2009-10-28 | 济南大学 | Zirconia ceramic matrix composite and preparation method thereof |
| CN101857455A (en) * | 2010-06-25 | 2010-10-13 | 中南大学 | High strength and toughness 3Y-TZP composite ceramic and preparation method thereof |
Non-Patent Citations (2)
| Title |
|---|
| XIU-PING ZHANG等: "Crack-healing ability and strength recovery of different hot-pressed TZ3Y20A–SiC ceramics by heat treatment in air", 《MATERIALS AND DESIGN》 * |
| XIU-PING ZHANG等: "Crack-healing behavior and strength recovery of hot-pressed TZ3Y20A–MoSi2 ceramics", 《MATERIALS SCIENCE&ENGINEERING A》 * |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108165929A (en) * | 2017-12-28 | 2018-06-15 | 中国科学院宁波材料技术与工程研究所 | A kind of self-healing coating and preparation method and application |
| CN108165929B (en) * | 2017-12-28 | 2019-10-11 | 中国科学院宁波材料技术与工程研究所 | A kind of self-healing coating and the preparation method and application thereof |
| CN108395223A (en) * | 2018-03-22 | 2018-08-14 | 中铭瓷(苏州)纳米粉体技术有限公司 | A kind of MAX phases crackle self-healing ceramic material and preparation method thereof |
| EP3885089A4 (en) * | 2018-12-21 | 2022-08-17 | Canon Kabushiki Kaisha | Powdered inorganic material and method for producing structure |
| CN116161951A (en) * | 2018-12-21 | 2023-05-26 | 佳能株式会社 | Inorganic material powder and method for producing structure |
| CN109608218A (en) * | 2019-01-28 | 2019-04-12 | 中国人民解放军国防科技大学 | Self-healing ceramic matrix composite and low-temperature rapid preparation method thereof |
| CN109608218B (en) * | 2019-01-28 | 2021-09-24 | 中国人民解放军国防科技大学 | Self-healing ceramic matrix composite and low-temperature rapid preparation method thereof |
| CN109987947A (en) * | 2019-04-19 | 2019-07-09 | 中国科学院上海硅酸盐研究所 | Utilize the thermally conductive method with mechanical property of in-situ stress induced transformation Synchronous fluorimetry aluminum oxide coating layer |
| CN111548164A (en) * | 2020-05-19 | 2020-08-18 | 中钢集团洛阳耐火材料研究院有限公司 | Continuous self-toughening nitride-bonded silicon carbide refractory material |
| CN113402263A (en) * | 2021-07-02 | 2021-09-17 | 海南大学 | Alumina-based composite ceramic and preparation method thereof |
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Application publication date: 20160127 |